Effect of Molecular Architecture on Phase Behavior of Graft Copolymers

Jul 17, 2008 - reciprocal-space self-consistent filed theory (SCFT). The phase diagrams were examined as functions of the architectural parameters ...
1 downloads 0 Views 413KB Size
Download PDF
9720

J. Phys. Chem. B 2008, 112, 9720–9728

Effect of Molecular Architecture on Phase Behavior of Graft Copolymers Liangshun Zhang, Jiaping Lin,* and Shaoliang Lin Key Laboratory for Ultrafine Materials of Ministry of Education, School of Materials Science and Engineering, East China UniVersity of Science and Technology, Shanghai 200237, China ReceiVed: March 31, 2008; ReVised Manuscript ReceiVed: May 15, 2008

Influence of molecular architecture on phase behavior of graft copolymer melts was studied by using a reciprocal-space self-consistent filed theory (SCFT). The phase diagrams were examined as functions of the architectural parameters describing the graft copolymers (i.e., the number of grafts and the position of first junction). In comparison with the well-known phase diagram of diblock copolymers, the phase diagrams of the graft copolymers are asymmetric. When the number of grafts or the position of first junction varies, the boundaries of order-order transitions have shifts due to the variation in the chain stretching energy. The change in molecular architecture also significantly alters the domain spacing of ordered structures but has weak impact on the density distributions of graft copolymers. For comparison of the theoretical predictions with the existing experimental results, the phase diagrams of graft copolymers were also calculated at strong segregation. The SCFT calculations can accurately capture the characteristics of the phase behavior of graft copolymer melts. Introduction The most important principles of block copolymer phase behavior have been already captured by the simplest AB diblock architecture.1–5 The microphase-separated structures of block copolymers are controlled by the delicate competition between the interaction energy and the chain stretching energy. The repulsion between the chemically different fragments drives the system to undergo phase separation; however, because the incompatible blocks are chemically connected, the system exhibits microphase separation and self-organizes into various ordered structures. For the simplest diblock copolymer melt, the ordered structures include lamella, bicontinuous gyroid, hexagonally packed cylinders, and body-centered cubic spheres. These equilibrium morphologies can be tailored by varying the copolymer composition f and the segregation degree χN between the two blocks (χ is the Flory-Huggins interaction parameter and N is the degree of polymerization). Because of the ongoing interest in novel macromolecular organization, well-defined nonlinear copolymers with complex architectures such as graft, starblock, miktoarm, and hyperbranched copolymers have been studied experimentally.6–10 It is shown that the molecular architecture is an important factor for tailoring the morphologies, phase behavior, and material properties. Among these copolymers with complex architecture, considerable attention has been paid to the microphase separation of graft copolymers because of their unique material properties and their applications as interface compatiblizers, thermoplastic elastomers, and viscosity modifiers.11–13 Gido, Hadjichristidis, Mays et al. synthesized a series of architecturally well-defined graft copolymers with a polyisoprene (PI) backbone and polystyrene (PS) graft chains.14–21 Well-ordered lamellar, cylindrical, and spherical morphologies are observed. The morphologies of graft copolymers and domain spacing of ordered structures depend on the molecular architecture of graft copolymers, such as the number of grafts and the distribution * Corresponding author. Tel: +86-21-64253370. Fax: +86-21-64253539. E-mail: [email protected].

of junctions. There is a dramatic shift in the phase boundaries of graft copolymer melts compared with diblock copolymers at the given segregation degree. To predict and interpret the architectural effect on the self-assembly behavior of graft copolymers, Gido et al. proposed a constituting block copolymer hypothesis.14–16 According to the hypothesis, the phase behavior of graft copolymers is dictated by the behavior of constituting block copolymers, which are formed by imaging all looped and bridged blocks of backbone to be cut in half. Existing Milner’s theory for star copolymers is used to predict the phase boundaries of the constituting block copolymers.22 The results of experimental studies for graft copolymers are in general agreement with the predictions of Milner’s phase diagram for the constituting block copolymers. However, the Milner’s phase diagram has a tendency to overestimate the copolymer composition for the order-order transitions. A variety of theoretical methods have been used to investigate the effect of molecular architecture on the phase behavior of graft copolymers.23–31 Olvera de la Cruz and Sanchez utilized random phase approximation (RPA) to study the order-disorder transition (ODT) of graft copolymers.23 The calculations indicated that the spinodal value (χN)s of symmetric graft copolymers has a larger value compared with (χN)s of corresponding diblock copolymers. In a related study, Balazs and co-workers investigated the microphase separation of graft copolymers with even or random distributions of junctions.24,25 They found that it is the χN value of the average constituting single graft copolymers which determines the proximity to the ODT. Chakraborty and co-workers developed a Landau fieldtheoretical model to study microphase separation in melts of randomly grafted copolymers.26–28 The stability regions of ordered phases strongly depend on the architectural parameters, such as the backbone length, the branch length, and the number of branches. Recently, Patel and Fredrickson constructed a field theory model of randomly graft copolymer melts.29 They carried out simulations of field theory for quenched and annealed cases by invoking the mean-field approximation. The main focus of their work was to clarify the conditions for which quenched

10.1021/jp802770z CCC: $40.75  2008 American Chemical Society Published on Web 07/17/2008

Phase Behavior of Graft Copolymers and annealed averages can be interchanged. These theoretical studies mentioned above mainly concentrate on the difference between graft copolymers and linear block copolymers. However, so far, one major unresolved issue regarding the graft copolymers is that the phase diagrams are not mapped out. The self-consistent field theory (SCFT) has emerged as a powerful tool to study the equilibrium thermodynamical features of polymers. The theory for polymer melts has its origin from the field theoretical approach of Edwards in the 1960s.32 Helfand and others explicitly adapted the theory to tackle the selfassembly behavior of block copolymers in subsequent decades.33–36 Recently, Matsen and Schick developed a state-ofthe-art numerical approach to solve the SCFT equations.3,37,38 In this method, a set of basis functions based on the assumed morphological symmetries are adopted to expand the fields. The Matsen-Schick approach is suited for the accurate calculations of free energy and the construction of phase diagrams. The phase diagrams of broad class of copolymer architectures have been mapped out by performing the SCFT calculations in reciprocal space.39–48 For example, Matsen and Schick examined the phase diagrams for melts of starblock copolymers with one, three, five, and nine arms.39 There is a preference for the inner blocks of the arms to be located in the inside of cylindrical and spherical phases. The preference increases with increasing number of arms. Grason and Kamien performed the self-consistent field theory for melts of star copolymers or multiply branched copolymers.46–48 Compared with the phase behavior of AB block copolymers, the phase boundaries for these copolymer melts are asymmetric. An alternative numerical approach to solve the SCFT equation was implemented in real space by Fredrickson et al.49–51 A prior assumption about the mesophase symmetry is not necessary. This method is found to be an efficient way to screen for new types of microstructures. In our previous work, we utilized the SCFT solved in real space to study the morphologies and bridging properties of graft copolymers in the bulk and aggregate morphologies of amphiphilic graft copolymers in dilute solution.52,53 In our model, the graft copolymers exhibit two distinctive architectural parameters: the number of grafts and the distribution of junctions. The morphological transitions can be triggered by varying the molecular architecture of graft copolymers. However, the thorough investigation on the phase behavior of graft copolymers was not carried out. The purpose of the present work is to systemically examine the phase behavior of graft copolymers by using a reciprocalspace SCFT approach. The architectural parameters, which are the number of grafts and the distribution of junctions, were incorporated in the model of graft copolymers. The phase diagrams for graft copolymers with various values of graft number and distribution of junctions were mapped out to determine the relationship between the phase behavior and molecular architecture. It was found that the variation in molecular architecture of graft copolymers can cause shifts in the phase boundaries and change the symmetry of phase diagrams. We also examined the effect of molecular architecture on the domain spacing of ordered structures and density distribution of graft copolymers. The theoretical predictions were compared with the existing experimental results, and a good agreement was exhibited. We expect that the present study may offer a fundamental insight about the molecular architecture effect on the self-assembly behavior of graft copolymers. Theoretical Framework For a canonical ensemble, nG graft copolymers are contained in a volume V. The molecular architecture of graft copolymers

J. Phys. Chem. B, Vol. 112, No. 32, 2008 9721

Figure 1. Molecular architecture of the graft copolymer.

is shown in Figure 1. z flexible homopolymer graft chains are spaced along a flexible homopolymer backbone. The backbone and graft chain are composed of NA A segments and NB B segments, respectively. Therefore, the number of total segments for single graft copolymer is NG ) NA + zNB. The A or B segment occupies a fixed volume F0-1, so that the total volume of the system with incompressibility equals to nGNG/F0. The statistical segment length a is assumed to be the same for both segments. The volume fraction of the A-type segment in the system is denoted by fA, and that of B-type segment is fB ) 1 - fA. The ith junction point is located at τi given by

τi ) τ1 +

(i - 1)(1 - 2τ1) z-1

1eiez

(1)

For the Gaussian chain model adopted in the present study and within the mean-field approximation, the statistics of the polymers is modeled by the configuration of the single polymer chain, which is determined by a set of effective chemical potential fields ωK(r)(K ) A, B), replacing the actual interactions within the bulks. These chemical potential fields are conjugated to the segment density fields φK(r). For such an A-g-Bz melt, the free energy per chain is given by

QG 1 F ) -ln + nGkBT V V

∫ dr[χABNGφA(r)φB(r) -

ωA(r)φA(r) - ωB(r)φB(r) - ξ(r)(1 - φA(r) - φB(r))] (2) Here, χAB denotes the Flory-Huggins parameter, characterizing the repulsive interaction between the A- and B-type segments. The function ξ(r) is Lagrangian multiplier to enforce the incompressibility condition (φA(r) + φB(r) ) 1). QG is the partition function of a single noninteracting, grafted chain subject to the chemical potential fields ωA(r) and ωB(r) in terms of the backbone propagator qA(r,s). The variable s is proportional to the arc length along the contour of the polymer, where s is scaled by NA for backbone and NB for graft chains. The spatial coordinate r is in units of Rg, where Rg2 ) NGa2/6. The backbone propagator is divided into z + 1 blocks

qA(r, s) ) qA(g)(r, s) for

τg e s < τg+1

g ) 0, 1, ... , z τ0 ≡ 1,

τz+1 ≡ 1 (3)

where each block satisfies the modified diffusion equation

NG ∂qA(g)(r, s) ) ∇2qA(g)(r, s) - ωA(r)qA(g)(r, s) NA ∂s

(4)

The equation is subject to the following initial condition

qA(g)(r, τg) ) qA(g-1)(r, τg )qB(r, 1)

g ) 1, 2, ... , z q(0) A (r, 0) ) 1 (5)

where qA(g-1)(r, τ-g) is the limit of the function as s approaches τg from below (just after the junction point). qB(r, s) is a

9722 J. Phys. Chem. B, Vol. 112, No. 32, 2008

Zhang et al.

propagator for graft chains, which is the solution of the modified diffusion equation

NG ∂qB(r, s) ) ∇2qB(r, s) - ωB(r)qB(r, s) NB ∂s

(6)

with the initial condition qB(r, 0) ) 1 for the free end of the graft chains at s ) 0. In terms of the backbone propagator qA(r, s), we can compute the single chain partition function

QG )

∫ drqA(r, 1)

(7)

In addition, we also define a backward propagator of the gth graft chain qj(g) B (r, s), which satisfies the same diffusion equation qB(r, s) with the right-hand side multiplied by -1, but starts on the junction point of the graft chain and is subject to the initial condition (z-g) qB(g)(r, 1) ) qA(g-1)(r, τ(r, (1 - τg)-) g )qA

(8)

Minimization of the free energy F, with respect to φA(r), φB(r), ωA(r), ωB(r), and ξ(r), is achieved by satisfying a set of mean-field equations

ωA(r) ) χABNGφB(r) + ξ(r)

(9)

ωB(r) ) χABNGφA(r) + ξ(r)

(10)

φA(r) ) -

V δQG QG δωA(r)

(11)

φB(r) ) -

V δQG QG δωB(r)

(12)

φA(r) + φB(r) ) 1

(13)

In terms of these propagators, the segment densities φA(r) and φB(r) are given by

φA(r) )

VfA z QG g)0

φB(r) )

∑ ∫τ

τg+1 g

VfB z mQG g)1

dsqA(g)(r, s)qA(z-g)(r, 1 - s)

∑ ∫0 dsqB(r, s)qB(g)(r, s) 1

(14)

(15)

In our previous study, the real-space method for numerically solving the SCFT equations was adopted.52–54 While the method provides an efficient approach to search for the ordered structures, the method tends to be computationally intensive for melt phase with spatial variation in three dimensions. Instead, we use the reciprocal space method invented by Matsen and Schick,3 which allows for the rapid and very accurate exploration of mean-field thermodynamics. The method utilizes the symmetry properties of the ordered structures. A set of basis functions fn(r) are used to span the function space and solve qA(r, s), qB(r, s), and q(g) B (r, s) at an arbitrary set of external fields. Details of the reciprocal method of SCFT for graft copolymers are presented in the Appendix. Results A. Phase Diagram. The phase diagrams were constructed by comparing the free energies of the different microphase separated structures and choosing the one with the minimal free energy as the equilibrium structure. The free energy for an ordered structure has to be minimized with respect to the periodicity D/Rg of the structure. In the reciprocal space method, the symmetries of the ordered structures are chosen a priori.55 In our present study, because our main aim is to examine the

Figure 2. Mean-field phase diagrams for graft copolymers with various molecular architectures (a) z ) 2, and τ1 ) 0.05; (b) z ) 2, and τ1 ) 0.33. Dis labels the regions where the melt is disordered. The ordered regions are denoted as S (body-centered cubic spheres, Im3jm symmetry), C (hexagonally packed cylinders, P6mm symmetry), G (bicontinuous gyroid, Ia3jd symmetry), and L (Lamella). The solid lines represent the phase boundaries between different phases. The subscript A and B of G, C, and S represent that the minority domains are occupied by the A and B blocks, respectively.

effect of molecular architecture on the phase behavior of graft copolymers, the stable structures considered include lamella (L), bicontinuous gyroid (G), hexagonally packed cylinders (C), and body-centered cubic spheres (S). In addition, the two-phase coexistence regions around the phase boundaries are neglected in our calculations for simplicity. Figure 2 shows the mean-field phase diagrams of graft copolymers with the first junction point τ1 ) 0.05 and τ1 ) 0.33 at the graft number z ) 2. In the phase diagrams, the vertical axis is the interaction strength χABNG/z of the average constituting single graft copolymer. The solid lines represent the phase boundaries between different phases. The ordered phases are labeled as L (Lamella), G (Gyroid), C (Cylinder), and S (Sphere). The subscript A and B of G, C, and S represent that the minority domains are occupied by the A and B blocks, respectively. As the volume fraction fA of backbone increases in the phase diagrams from left to right, the sequence of ordered phases follows: SA-CA-GA-L-GB-CB-SB. One notable feature of these phase diagrams is that they are not symmetrical about fA ) 0.50. For τ1 ) 0.05, the phases (SA, CA, and GA) with the backbone blocks in the minority domains occupy a wide range of fA for a given χABNG/z, while the regions of ordered phases (GB, CB, and SB) with backbone blocks forming the matrix are narrow (as shown in Figure 2a). For τ1 ) 0.33, another scenario is observed in Figure 2b. The regions of phases (GB, CB, and SB) are wider than those of phases (GA, CA, and SA) for a given χABNG/z. The triple points, which are at the intersection of C, G, and L phases, are also not symmetrical. Another feature of the phase diagrams is that the order-disorder transition (ODT) is dramatically altered by the position of the first junction point as can be seen from the comparison between Figure 2a and 2b. The critical point of graft copolymer melts, which indicates a second-order transition from the disordered state to lamellar phase, is shifted when τ1 changes, for example, χABNG/z ) 9.91

Phase Behavior of Graft Copolymers

Figure 3. Mean-field phase diagrams for graft copolymers with various molecular architectures (a) z ) 3, and τ1 ) 0.05; (b) z ) 3, and τ1 ) 0.33. Labels appear as in Figure 2.

and fA ) 0.497 for τ1 ) 0.05; and χABNG/z ) 12.34 and fA ) 0.412 for τ1 ) 0.33. The SCFT phase diagrams of graft copolymers with the first junction point τ1 ) 0.05 and τ1 ) 0.33 at z ) 3 are illustrated in Figure 3. Similarly, the architecture parameters have a significant impact on the phase diagrams of graft copolymers at z ) 3. The phase diagrams of the graft copolymers at z ) 3 are also asymmetric. The critical point shifts toward one side of ODT. The triple points also have a shift and are tilted. It can be seen that the regions of stability structures and phase boundaries have a marked change as the graft number increases 2 to 3. Since τ1 and z exert a marked effect on the phase behavior of the graft copolymers, it is instructive to plot phase diagrams of the graft copolymer melts, in which the first junction position (τ1) or graft number (z) versus the volume fraction of backbone (fA) plane is plotted at a fixed degree of segregation (χABNG/z). Phase diagrams in τ1 versus fA space for graft copolymers with z ) 2 and z ) 3 at χABNG/z ) 18.0 are shown in Figure 4. The ordered phase region tends to be narrow at the intermediate values of τ1. The stable regions of SA, CA, and GA, where the backbone blocks form the minority domains, have a minimum at the intermediate values of τ1. However, the stable regions of SB, CB, and GB, where the backbone blocks produce the matrix, have a maximum at the intermediate values of τ1. There are strong shifts in boundaries of order-order transitions (OOTs) first to the left and then to the right as the τ1 value increases except for SA-CA boundary. In the region of smaller τ1, the boundaries of OOTs tend to shift toward smaller values of fA with increasing the value of τ1. In the region of larger τ1, increasing the τ1 value gives rise to the shift toward larger values of fA. In the region of intermediate τ1, the effect of τ1 on the boundaries of OOTs is not significant. The shifts of OOTs induced by variation of the first junction position can result in some novel transition sequences, which is different from the transition order induced by the volume fraction of backbone. For example, the transition sequence of L-GB-CB-GB-L is triggered by changing the first junction position τ1 from zero to 0.5 at z ) 2, fA ) 0.58, and χABNG/z ) 18.0, which is traced out by an arrow in Figure 4a.

J. Phys. Chem. B, Vol. 112, No. 32, 2008 9723

Figure 4. Mean-field phase diagrams in τ1-fA space for graft copolymers with (a) z ) 2 and (b) z ) 3 at χABNG/z ) 18.0. Labels appear as in Figure 2.

Figure 5. Mean-field phase diagram in z-fA space for graft copolymers with τ1 ) 0.05 at χABNG/z ) 18.0. Labels appear as in Figure 2.

Figure 6. Mean-field phase diagram in z-fA space for graft copolymers with τ1 ) 0.30 at χABNG/z ) 18.0. Labels appear as in Figure 2.

From Figure 4a and 4b, the influence of graft number on phase behavior can also be viewed. In the region of smaller τ1, the phase boundaries tend to shift toward smaller values of fA as z increases from 2 to 3. In the region of larger τ1, the phase boundaries tend to shift toward larger values of fA with increasing z. In the region of intermediate τ1, the effect of z on the phase boundaries is not marked. The effect of graft number on phase behavior in the smaller, larger, intermediate regions of τ1 can be further viewed in Figures 5, 6, and 7, respectively. Figure 5 illustrates the mean-field phase diagram in z-fA space for graft copolymers with τ1 ) 0.05 at χABNG/z ) 18.0. For graft copolymers with z ) 2 and z ) 3, the stable ordered phase regions including SA, CA, and GA, where the backbone blocks form the minority domain, are broader than those of their

9724 J. Phys. Chem. B, Vol. 112, No. 32, 2008

Figure 7. Mean-field phase diagrams in z-fA space for graft copolymers with (a) τ1 ) 1/(z + 1) and (b) τ1 ) 1/2z at χABNG/z ) 18.0. Labels appear as in Figure 2.

corresponding reverse phases. An increase in the number of grafts shrinks the phase regions (SA, CA, and GA) but enlarges the regions of their corresponding reverse phases. As z is above 4, the phases (SB, CB, and GB) with the backbone blocks outside of curved interfaces are favored. The OOTs shift toward the smaller fA values when z increases from 2 to 6. Figure 6 displays the phase diagram plotted in z versus fA plane for graft copolymers with larger τ1 value at fixed χABNG/z ) 18.0.The stability regions of morphologies (SA, CA, and GA) with backbone in the inside of curved interface are suppressed at z ) 2. However, the stability regions of these phases are enlarged because of the additional asymmetry introduced by increasing the graft number. The ordered phases with backbone in the inside of the curved interface are favored at z ) 5. The volume fractions of OOTs tend to shift toward the larger values of fA as z increases. As for the influence of graft number at the intermediate value of τ1, two cases in terms of the junction distribution are calculated. On is that τ1 is set to be 1/(z + 1). Under this condition, the length of inner blocks between neighbor junctions is equal to that of free end blocks. The other case is that τ1 is taken to be 1/(2z). With this adoption of τ1, the constituting block copolymers by cutting the middle point of the connecting blocks are the symmetric single graft architectures. Figure 7 shows the z-fA phase diagrams for graft copolymers with τ1 ) 1/(z+1) and τ1 ) 1/(2z) at χABNG/z ) 18.0. The phases (SB, CB, and GB) with the backbone blocks in the outside of curved interface are more favored. The phase boundaries of L-GB, GBCB, and CB-SB are almost invariable as the graft number changes. However, the phase boundaries of SA-CA, CA-GA, and GA-L have a slight shift toward smaller values of fA as the graft number increases. The different between panels a and b in Figure 7 is small. This can also be viewed in Figure 4 that the effect of τ1 on the phase boundaries of graft copolymers is not marked at intermediate values of τ1. B. Density Distribution and Domain Spacing. A useful feature of SCFT is that it yields the density distribution and domain spacing, which are associated with the various properties of graft copolymers. Figure 8a shows the A-segment volume fraction profiles in lamellar phase for graft copolymers with

Zhang et al.

Figure 8. (a) A-segment volume fraction profiles in lamellar phase for graft copolymers with τ1 ) 0.02 (full line), 0.25 (dash line), and 0.45 (dot line) at z ) 2, χABNG/z ) 18.0, and fA ) 0.48. The equilibrium length scales D are 2.89Rg, 2.45Rg, and 2.74Rg, for τ1 ) 0.02, 0.25, and 0.45, respectively. (b) A-segment volume fraction profiles in lamellar phase for graft copolymers with z ) 2 (full line), 4 (dash line), and 6 (dot line) at τ1 ) 0.30, χABNG/z ) 18.0, and fA ) 0.48. The equilibrium length scales D are 2.44Rg, 1.87Rg, and 1.66Rg, for z ) 2, 4, and 6, respectively.

τ1 ) 0.02, 0.25, and 0.45 at z ) 2, χABNG/z ) 18.0, and fA ) 0.48. In comparison with τ1 at larger or smaller values, a slight decrease in segregation occurs when τ1 values are in the intermediate range. Figure 8b displays the A-segment volume fraction profiles in lamellar phase for graft copolymers with z ) 2, 4, and 6. A slight increase in segregation takes place as z increases. In comparison with the thermodynamic parameters (volume fraction of block and degree of segregation), the architecture parameters of copolymers has a weak impact on the density distribution of graft copolymers. Figure 9a illustrates the period D/Rg of the lamellar phase as a function of the first junction position at fA ) 0.48 and χABNG/z ) 18.0 for z ) 2 and 3. At smaller τ1 values, D/Rg decreases with increasing τ1. As τ1 increases, the change in D/Rg becomes less marked. With further increasing τ1, D/Rg increases. It is also noted that the lamellar phase period of the graft copolymers with smaller z is greater than that having larger z. When τ1 is smaller, the domain spacing is mainly controlled by the length of inner blocks. The length of inner blocks becomes shorter, and the domain spacing decreases with an increase in τ1. When τ1 is in the intermediate range, the period of lamellar phase reaches a minimum. The period slowly changes at the intermediate range of τ1 because of the competition between the lengths of free end blocks and inner blocks. When τ1 is larger, the free end blocks are the longest ones that determine the domain spacing. As τ1 further increases, the domain spacing has a significant increase. Figure 9b shows the lamellar period D/Rg as a function of the number of grafts at fA ) 0.48 and χABNG/z ) 18.0 for τ1 ) 0.05 and τ1 ) 0.30. Increasing the graft number gives rise to a decrease in the domain spacing. This trend can be ascribed to the fact that the average lengths of graft chains and backbone blocks become short as the graft number increases.

Phase Behavior of Graft Copolymers

J. Phys. Chem. B, Vol. 112, No. 32, 2008 9725

Figure 10. Schematic representations of graft copolymers on an interface. (a) Graft copolymer with a smaller value of τ1 at a flat interface; (b) graft copolymer with a intermediate value of τ1 at a curved interface; (c) graft copolymer with a larger value of τ1 at a flat interface. The curvature interface is exaggerated.

Figure 9. (a) Lamellar period D/Rg as a function of the first junction position τ1 at fA ) 0.48 and χABNG/z ) 18.0 for z ) 2 and z ) 3. (b) Lamellar period D/Rg as a function of the graft number z at fA ) 0.48 and χABNG/z ) 18.0 for τ1 ) 0.05 and τ1 ) 0.30.

Discussion Although the topology of the phase diagrams for graft copolymers is equivalent to that of the standard AB diblock copolymer melts, SCFT predicts several significant differences (as shown Figures 2 and 3). For the classic phase diagram of diblock copolymers,3 it is plotted in χABN-fA space and is symmetric about fA ) 0.50. With respective to the graft copolymers, the vertical axis of phase diagrams is the interaction strength χABNG/z of the average constituting single graft copolymers. Because of the additional asymmetry introduced by molecular architecture, change from the diblock copolymers to graft copolymers breaks the fA T 1 - fA symmetry of the phase diagrams. The phase behavior of diblock copolymers is determined by the copolymer composition and segregation degree. For the graft copolymers, in addition to these two parameters, the architecture parameters (the graft number and junction distribution) exert a significant effect on the phase boundaries and stability regions of phase diagrams. Another distinct difference between diblock copolymers and graft copolymers is that the graft copolymers have junctions along the backbone constrained to the domain interfaces. The backbone blocks of graft copolymers can take either looped conformation whose neighbor junctions locate in the same domain or bridged conformation whose neighbor junctions are anchored on the different domain interfaces. The existence of bridged blocks linking separate domains strongly affects the mechanical properties of the graft copolymers at fracture. Therefore, the fraction of bridged conformation is a crucial parameter for material design. In our previous study, we have investigated the bridged and looped conformation of the backbone of the graft copolymer by using self-consistent field theory.52 The fraction of bridged conformation has a tendency to decrease with increasing the length of free end blocks and the number of grafts. The number of bridged chains per unit area increases with increasing the number of grafts in the cylindrical phase. But in the lamellar phase, it decreases when the graft number increases. The phase diagrams of graft copolymer melts strongly depend on the first junction position and graft number (as shown in

Figures 4–7). This behavior can be rationalized by considering the stretching energy of the chains. The backbone of graft copolymers is composed of two different length blocks (free end blocks and inner blocks). The graft copolymers with a smaller τ1 (larger τ1) value have the longer length of inner (free end) blocks. The availability of longer and shorter blocks capable of filling the interstitial regions can relieve the excessive stretching and compression (as shown in Figure 10a and 10c). When τ1 becomes intermediate, the asymmetry of free and inner blocks of backbone becomes small and the blocks become overcrowded. Since the polymer chains must be adjusted to maintain a constant density for an incompressible system,45 the free end blocks and inner blocks have to be stretched away from the interface and compressed close to the interface. The lateral crowding and additional chain stretching can be partially alleviated by allowing the interface to curve away form backbone domain. These result in an enhanced preference for backbone to remain on the convex side of the interface, which is illustrated in Figure 10b. Such a preference causes the shifts of OOT lines toward lower backbone block volume fraction in the intermediate region of τ1 (as shown in Figure 4).16 Similarly, the inner blocks become overcrowded because of the junction constraint of the backbone as the graft number increases (fixed the τ1 at smaller value). To alleviate the crowding and stretching of inner blocks and lower the total free energy, the interface curves away from backbone domain. This change in the spontaneous curvature shifts the OOTs toward smaller fA as the graft number increases (Figure 5). The graft copolymers with larger τ1 values, which have the shorter length of inner blocks, can be regarded as the star copolymers. The graft chains become overcrowded as the graft number increases. Consequently, the interface curves away from graft chain domain. This results in the shifts in OOTs toward the larger fA values as the graft number increases (as shown in Figure 6). At intermediate τ1 values, the phase boundaries of OOTs tend to be invariable as the graft number increases (as shown in Figure 7), because the length difference of free end blocks and inner blocks is small. Some experimental evidence are available in the literature, supporting the predicted results of SCFT for graft copolymer melts. Gido et al. synthesized a series of well-defined graft copolymers with polyisoprene (PI) backbone and polystyrene (PS) branches (PS-g-PI).14–21 They can precisely control over the backbone molecular weight, arm molecular weight, arm polydispersity, and placement of junction points, etc. The microphase separation of graft copolymers was observed, and the classical microdomian geometries of lamella, cylinder, and sphere were identified. For comparison with the experiments, we calculated the phase diagram of graft copolymers at strong segregation in accord

9726 J. Phys. Chem. B, Vol. 112, No. 32, 2008

Zhang et al. cially in the phase regions where the minority domains are formed by the backbone. The reason for the overestimation could be ascribed to a junction point delocalization effect at the AB interface, which is neglected in Milner’s calculations.16 In real case, the junction points of A and B blocks may delocalize from the interface,47 while in Milner’s theory they are assumed to be confined to the interface. As can been seen from above discussion, SCFT in comparison with the Milner’s theory can more accurately capture the characteristics of the phase behaviors of the graft copolymers.

Figure 11. Comparison of the SCFT results with the experimental findings at strong segregation. The solid lines represent the phase boundaries between different phases obtained from the SCFT calculation of graft copolymers with τ1 ) 1/2z at χABNG/z ) 80.0. The filled symbols indicate the results from the experiments of polystyrene-gpolyisoprene graft copolymer melts.16,17,21 (9) Lamellar phase, (2) cylindrical phase, (b) spherical phase, and (1) disordered state. The hollow symbols represent the transition points between different phases calculated according to Milner’s theory.22 (0) S-C transitions, and (O) C-L transitions.

with the strong incompatibility of PS and PI.17 Because of the numerical difficulties of the considered gyroid phase for large χABNG/z, the gyroid phase is not included in the phase diagram. In our calculations, the boundaries of disorder-sphere, sphere-cylinder, and cylinder-lamella transitions are evaluated. Figure 11 illustrates the SCFT z-fA phase diagram of graft copolymers with τ1 ) 1/(2z) at χABNG/z ) 80.0. The phase boundaries calculated by SCFT are represented by the solid lines. In Figure 11, the results from the experiments of graft copolymers with regularly spaced junction points are also presented.16,17,21 The vertical and horizontal axes of phase diagram correspond to the number of junction points per molecule and the volume fraction of polyisoprene in experiments, respectively. The filled symbols in Figure 11 indicate the experimentally observed morphologies. Our phase diagram calculated by SCFT is in good agreement with the experimental results of PS-g-PI graft copolymer melts. One exception is that the lamellar phases formed by graft copolymers with 56 vol% PI are located in the cylindrical phase region of theoretical phase diagram. But the discrepancy between the experiment and prediction is small. Such a difference could be attributed to a number of factors associated with our simple model (not consider the fluctuation effects, actual sizes of the monomers, and the random distribution of junction points) and sample polydispersity. As for the theoretical considerations of the phase behavior of graft copolymers, Gido et al. prescribed an empirical method.14–21 It was proposed that the morphologies of graft copolymers are governed by the behavior of constituting block copolymers, which is a single-graft architecture by cutting the connecting blocks of backbone at the middle. The single-graft copolymers can be regarded as A2B star architecture. Existing Milner’s theory in strong segregation limit is used to capture the phase behavior of AnBm star copolymers.22 This theory predicts the phase boundaries as functions of the component volume fraction and molecular asymmetry parameter. For the PS-g-PI graft copolymers studied by Gido et al., the molecular asymmetry parameter of single-graft copolymers was calculated to be 1.78.15 The sphere-cylinder and cylinder-lamella transition points calculated by Milner’s theory are also presented in the phase diagram (as shown in Figure 11). The general tendency of Milner’s predictions is in agreement with the experimental results. However, in comparison with our calculations, the Milner’s prediction has some degree of overestimation, espe-

Conclusion In this study, we examined the phase behavior of graft copolymer melts using the reciprocal-space self-consistent field theory. The χABNG/z-fA space phase diagrams for graft copolymers with various molecular architectures were constructed by comparing the computed free energy of different phases. In comparison with the AB diblock copolymers, the phase boundaries become asymmetric about fA ) 0.50. We also mapped out the phase diagrams of τ1-fA space and z-fA space. There are shifts in phase boundaries of OOTs first to the smaller values of fA and then to the larger values of fA as the first junction position τ1 changes from zero to 0.5. In the region of smaller τ1, the boundaries of OOTs shift toward the smaller values of fA as the graft number z increases. In the region of larger τ1, the boundaries of OOTs shift toward the larger values of fA with increasing the graft number. In the region of intermediate τ1, the shifts of phase boundaries are small when the graft number changes. In addition, the molecular architecture of graft copolymers significantly alters the domain spacing of ordered structures but has weak impact on the density profiles of respective components.The theoretical results obtained by the self-consistent field theory calculations in the strong segregation were compared with the existing experimental findings, and a good agreement was found. Acknowledgment. This work was supported by National Natural Science Foundation of China (50673026, 20574018). Support from Doctoral Foundation of Education Ministry of China (Grant No. 20050251008), Program for New Century Excellent Talents in University in China (NCET-04-0410), and Projects of Shanghai Municipality (06SU07002, 0652nm021, 082231, and B502) are also appreciated. Appendix. Spectral Solution to SCFT Equations In this appendix, we present details of numerical solution to SCFT equations in reciprocal space. For a periodic ordered phase, all functions of position vector r are expanded in a Fourier-like series

g(r) )

∑ gifi(r)

(A1)

i

The appropriate basis functions for the expansion are the eigenfunctions fi(r) of Laplace operator

∇2fi(r) ) -

λi D2

fi(r)

(A2)

where D is the length scale of the periodicity of the system. By convention, f0(r) ) 1 (or λ1 ) 0), and the eigenfunctions are ordered in an nondecreasing sequence of λi. In addition, the set of functions are normalized

Phase Behavior of Graft Copolymers

1 V

J. Phys. Chem. B, Vol. 112, No. 32, 2008 9727

∫ drfi(r)fj(r) ) δij

We can also write the product of two basis functions (fi(r) fj(r)) as expansion in our basis functions

fi(r)fj(r) )

∑ Γijkfk(r)

(A4)

k

Here, Γijk is the coefficient of the expansion. Alternately, those coefficients can be computed by Γijk ) V-1∫ dr fi(r) fj(r)fk(r). With these definitions and the Fourier expansions of functions, the partial differential equation becomes a differential equation form

dqB,i(s) ) ds

∑ BijqB,j(s)

(g) qjB,j (1)

where given by

(g) qB,j (1) )

∑ qA,j(τ-g )qA,k((1 - τg)-)Γijk

(A6)

where TB(s′) ) exp(Bs′) is the matrix that transfers qB,i(s) a distance s′ along the graft chain. Since the matrix B is symmetric and real, the matrix can be computed by performing an orthogonal transformation that diagonalizes B, such that B ) UBΛBUTB, where ΛB ) diag(λB,1,λB,2,..., λB,n) is the eigenvalues of B, UB ) {uB,1,uB,2,..., uB,n} is the eigenvectors of B. Therefore, T ∑ uB,ikexp(λB,ks)uB,kj

(A7)

Once q(g) j(g) A,i(s), qB,i(s), and q B,i(s) are solved with respect to ωA,i and ωB,i, the Fourier amplitudes of the segment densities φA,i and φB,i can be given by

φA,i )

fA z qA,1(1) g)0

∑ ∫τ

(g) dqA,i (s) ) ds

(g) (s) ∑ AijqA,i

(A8)

j

where Aij ) (-λiδij/D2 - ∑k ωA,kΓijk)NA/NG. The solution for qA(r, s) is given by (g) (g) qA,i (s) ) TA,ij(s - τg)qA,j (τg)

(A9)

where TA(s - τg) ) exp(A(s - τg)) is a matrix that transfers the solution from τg to s for the backbone. To evaluate the matrix, we diagonalize A by orthogonal transformation, such that A ) UAΛAUAT , where ΛA ) diag(λA,1,λA,2,..., λA,n) is the eigenvalues of A, UA ) {uA,1,uA,2,..., uA,n} is the eigenvectors of A. Using these matrixes, we can write the solution (g) qA,i (s) ) uA,ik

T (g) exp(λA,k(s - τg))uA,kj qA,j (τg)

(A10)

(g) (g) where qA,i (τg) are the boundary conditions for qA,i (s) at τg

(g) qA,i (τg) )

(g-1) (τg )qB,k(1)Γijk ∑ qA,j

τg+1 g

ds

(g) (z-g) (s)qA,k (1 - s)Γijk ∑ qA,j j,k

(A14) φB,i )

fB

g ) 1, 2, ... , z

j,k

(A11) (0) We use the fact that qA,i (0) ) δi1, which is the boundary (0) condition for the free end, is used to compute qA,i (s). We can (0) (1) then use eq A11 along qA,i(τg ) and qB,k(1) to find qA,i (s) for the block between τ1 and τ2. Repeating this process, we can find (g) (g) qA,i (τg) and qA,i (s) for all blocks. In addition, we also can compute the single-chain partition function Q ) VqA,1(1). (g) To obtain qjB,i (s), we solve the same matrix equations as eq A5 with a plus sign on the right-hand side. The solution for (g) qjB,i (s) is

z

(g) (s)Γijk ∑ ∫0 ds∑ qB,j(s)qB,k

mqA,1(1) g)1

1

(A15)

j,k

Finally, the free energy per chain is

F ) -ln qA,1(1) - χABNG nGkBT

∑ φA,iφB,i

(A16)

i

For the disordered phase, the free energy reads F/nGkBT ) χABNGfAfB. We adjust the assumed amplitudes ωA,i and ωB,i of the fields, so that the densities calculated above satisfy the self-consistency relations

ωA,i - ωB,i ) χABNG(φB,i - φA,i)

(A17)

φA,i + φB,i ) δi1

(A18)

k

Similarly, the diffusion equation for qA(r, s) becomes

(A13)

j,k

(A5)

qB,i(s) ) TB,i1(s)

(A12)

are the boundary conditions of junction points

j

where the matrix B is given by Bij ) (-λiδij/D2 - ∑k ωB,kΓijk)NB/NG, and the initial condition is qB,i(0) ) δi1. The solution to the set of linear differential equations is

TB,ij(s) )

(g) T (g) qB,i (s) ) uB,ik exp(λB,k(1 - s))uB,kj qB,j (1)

(A3)

The set of SCFT equations are highly nonlinear because the segment density amplitudes, φA,i and φB,i, depend functionally on the field amplitudes, ωA,i and ωB,i. For some initial values of ωA,i and ωB,i, the segment density amplitudes, φA,i and φB,i are computed by eqs A14 and A15, respectively. Then, ωA,i and ωB,i can be updated by Anderson mixing scheme.56 The above computation procedure is repeated until the self-consistent solution is found. The free energy of the ordered phase has to be minimized with respect to the periodicity of the structure. The phase diagrams are obtained by comparing the free energies of different structures and choosing the one with the minimal free energy as the equilibrium structures. References and Notes (1) Leibler, L. Macromolecules 1980, 13, 1602. (2) Semenov, A. N. SoV. Phys. JETP 1985, 61, 733. (3) Matsen, M. W.; Schick, M. Phys. ReV. Lett. 1994, 72, 2660. (4) Hamley, I. W. The Physics of Block Copolymers; Oxford University Press: New York, 1998. (5) Bates, F. S.; Fredrickson, G. H. Phys. Today 1999, 52, 32. (6) Hadjichristidis, N.; Iatrou, H.; Pitsikalis, M.; Pispas, S.; Avgeropoulos, A. Prog. Polym. Sci. 2005, 30, 725. (7) Hadjichristidis, N.; Iatrou, H.; Pitsikalis, M.; Mays, J. W. Prog. Polym. Sci. 2006, 31, 1068. (8) Pitsikalis, M.; Pispas, S.; Mays, J. W.; Hadjichristidis, N. AdV. Polym. Sci. 1998, 135, 1. (9) Hadjichristidis, N.; Pispas, S.; Pitsikalis, M.; Iatrou, H.; Vlahos, C. AdV. Polym. Sci. 1999, 142, 71. (10) Hadjichristidis, N.; Pitsikalis, M.; Iatrou, H. AdV. Polym. Sci. 2005, 189, 1. (11) Gersappe, D.; Irvie, D.; Balazs, A. C.; Liu, Y.; Sokolov, J.; Rafailovich, M.; Schwarz, S.; Peiffer, D. G. Science 1994, 265, 1072. (12) Kennedy, J. P.; Delvaux, J. M. AdV. Polym. Sci. 1991, 38, 141. (13) Kennedy, J. P. In Thermoplastic Elastomers; Legge, N. R., Holden, G., Quirk, R., Schroeder, H. E., Eds.; Hanser: Munich, 1996. (14) Gido, S. P.; Lee, C.; Pochan, D. J.; Pispas, S.; Mays, J. W.; Hadjichristidis, N. Macromolecules 1996, 29, 7022.

9728 J. Phys. Chem. B, Vol. 112, No. 32, 2008 (15) Lee, C.; Gido, S. P.; Poulos, Y.; Hadjichristidis, N.; Tan, N. B.; Trevino, S. F.; Mays, J. W. J. Chem. Phys. 1997, 107, 6460. (16) Lee, C.; Gido, S. P.; Poulos, Y.; Hadjichristidis, N.; Tan, N. B.; Trevino, S. F.; Mays, J. W. Polymer 1998, 39, 4631. (17) Xenidou, M.; Beyer, F. L.; Hadjichristidis, N.; Gido, S. P.; Tan, N. B. Macromolecules 1998, 31, 7659. (18) Beyer, F. L.; Gido, S. P.; Buschl, C.; Iatrou, H.; Uhrig, D.; Mays, J. W.; Chang, M. Y.; Garetz, B. A.; Balsara, N. P.; Tan, N. B.; Hadjichristidis, N. Macromolecules 2000, 33, 2039. (19) Weidisch, R.; Gido, S. P.; Uhrig, D.; Iatrou, H.; Mays, J. W.; Hadjichristidis, N. Macromolecules 2001, 34, 6333. (20) Zhu, Y.; Weidisch, R.; Gido, S. P.; Velis, G.; Hadjichristidis, N. Macromolecules 2002, 35, 5903. (21) Zhu, Y.; Burgaz, E.; Gido, S. P.; Staudinger, U.; Weidisch, R.; Uhrig, D.; Mays, J. W. Macromolecules 2006, 39, 4428. (22) Milner, S. T. Macromolecules 1994, 27, 2333. (23) Olvera de la Cruz, M.; Sanchez, I. C. Macromolecules 1996, 19, 2501. (24) Shinozaki, A.; Jasnow, D.; Balazs, A. C. Macromolecules 1994, 27, 2496. (25) Foster, D. P.; Jasnow, D.; Balazs, A. C. Macromolecules 1995, 28, 3450. (26) Qi, S.; Chakraborty, A. K.; Wang, H.; Lefebvre, A. A.; Balsara, N. P.; Shakhnovich, E. I.; Xenidou, M.; Hadjichristidis, N. Phys. ReV. Lett. 1999, 82, 2896. (27) Qi, S.; Chakraborty, A. K.; Balsara, N. P. J. Chem. Phys. 2001, 115, 3387. (28) Qi, S.; Chakraborty, A. K. J. Chem. Phys. 2001, 115, 3401. (29) Patel, D. M.; Fredrickosn, G. H. Phys. ReV. E 2003, 68, 051802. (30) Ye, X.; Shi, T.; Lu, Z.; Zhang, C.; Sun, Z.; An, L. Macromolecules 2005, 38, 8853. (31) Wang, R.; Jiang, Z.; Hu, J. Polymer 2005, 46, 6201. (32) Edwards, S. F. Proc. Phys. Soc. 1965, 85, 613.

Zhang et al. (33) Helfand, E. J. Chem. Phys. 1975, 62, 999. (34) Helfand, E.; Wasserman, Z. R. Macromolecules 1976, 9, 879. (35) Hong, K. M.; Noolandi, J. Macromolecules 1981, 14, 727. (36) Vavasour, J. D.; Whitmore, M. D. Macromolecules 1992, 25, 5477. (37) Matsen, M. W. J. Phys.: Condens. Matter 2002, 14, R21. (38) Matsen, M. W. In Soft Matter; Gompper, G., Schick, M., Eds.; Wiley-VCH: Weinheim, Germany, 2005; Vol. 1, p 87. (39) Matsen, M. W.; Schick, M. Macromolecules 1994, 27, 6761. (40) Matsen, M. W.; Thompson, R. B. J. Chem. Phys. 1999, 111, 7139. (41) Matsen, M. W. J. Chem. Phys. 2000, 113, 5539. (42) Matsen, M. W. Phys. ReV. Lett. 2007, 99, 148304. (43) Tyler, C. A.; Qin, J.; Bates, F. S.; Morse, D. C. Macromolecules 2007, 40, 4654. (44) Jiang, R.; Jin, Q.; Li, B.; Ding, D.; Shi, A.-C. Macromolecules 2006, 39, 5891. (45) Cooke, D. M.; Shi, A,-C. Macromolecules 2006, 39, 6661. (46) Grason, G. M.; DiDonna, B. A.; Kamien, R. D. Phys. ReV. Lett. 2003, 91, 058304. (47) Grason, G. M.; Kamien, R. D. Macromolecules 2004, 37, 7371. (48) Grason, G. M.; Kamien, R. D. Phys. ReV. E 2005, 71, 051801. (49) Drolet, F.; Fredrickson, G. H. Phys. ReV. Lett. 1999, 83, 4317. (50) Fredrickson, G. H.; Ganesan, V.; Drolet, F. Macromolecules 2002, 35, 16. (51) Fredrickosn, G. H. The Equilibrium Theory of Inhomogeneous Polymers; Oxford University Press: Oxford, 2006. (52) Zhang, L.; Lin, J.; Lin, S. J. Phys. Chem. B 2007, 111, 351. (53) Zhang, L.; Lin, J.; Lin, S. J. Phys. Chem. B 2007, 111, 9209. (54) Zhang, L.; Lin, J.; Lin, S. Macromolecules 2007, 40, 5582. (55) International Tables for X-ray Crystallography; Henry, N. F. M., Lonsdale, K., Eds.; Kynoch: Birmingham, U. K., 1969; Vol. 1. (56) Eyert, V. J. Comput. Phys. 1996, 124, 271.

JP802770Z